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WO2002051764A2 - Verre borosilicate contenant de l'oxyde de zinc - Google Patents

Verre borosilicate contenant de l'oxyde de zinc Download PDF

Info

Publication number
WO2002051764A2
WO2002051764A2 PCT/EP2001/015065 EP0115065W WO02051764A2 WO 2002051764 A2 WO2002051764 A2 WO 2002051764A2 EP 0115065 W EP0115065 W EP 0115065W WO 02051764 A2 WO02051764 A2 WO 02051764A2
Authority
WO
WIPO (PCT)
Prior art keywords
glasses
weight
borosilicate glass
glass
glass according
Prior art date
Application number
PCT/EP2001/015065
Other languages
German (de)
English (en)
Other versions
WO2002051764A3 (fr
Inventor
Silke Wolff
Ute Wölfel
Jose Zimmer
Original Assignee
Schott Glas
Carl-Zeiss-Stiftung Trading As Schott Glas
Carl-Zeiss-Stiftung
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Schott Glas, Carl-Zeiss-Stiftung Trading As Schott Glas, Carl-Zeiss-Stiftung filed Critical Schott Glas
Priority to US10/451,227 priority Critical patent/US20040075086A1/en
Priority to AU2002237247A priority patent/AU2002237247A1/en
Publication of WO2002051764A2 publication Critical patent/WO2002051764A2/fr
Publication of WO2002051764A3 publication Critical patent/WO2002051764A3/fr

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C3/00—Glass compositions
    • C03C3/04—Glass compositions containing silica
    • C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
    • C03C3/089—Glass compositions containing silica with 40% to 90% silica, by weight containing boron
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C1/00—Ingredients generally applicable to manufacture of glasses, glazes, or vitreous enamels
    • C03C1/004—Refining agents
    • C—CHEMISTRY; METALLURGY
    • C03—GLASS; MINERAL OR SLAG WOOL
    • C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
    • C03C21/00—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface
    • C03C21/001—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions
    • C03C21/002—Treatment of glass, not in the form of fibres or filaments, by diffusing ions or metals in the surface in liquid phase, e.g. molten salts, solutions to perform ion-exchange between alkali ions
    • G—PHYSICS
    • G11—INFORMATION STORAGE
    • G11B—INFORMATION STORAGE BASED ON RELATIVE MOVEMENT BETWEEN RECORD CARRIER AND TRANSDUCER
    • G11B5/00—Recording by magnetisation or demagnetisation of a record carrier; Reproducing by magnetic means; Record carriers therefor
    • G11B5/62—Record carriers characterised by the selection of the material
    • G11B5/73—Base layers, i.e. all non-magnetic layers lying under a lowermost magnetic recording layer, e.g. including any non-magnetic layer in between a first magnetic recording layer and either an underlying substrate or a soft magnetic underlayer
    • G11B5/739—Magnetic recording media substrates
    • G11B5/73911—Inorganic substrates
    • G11B5/73921—Glass or ceramic substrates

Definitions

  • the invention relates to a zinc oxide-containing borosilicate glass and uses of this glass.
  • glass is opposite metals such as aluminum or metal alloys. a. advantageous because of its flatness and low surface roughness.
  • substrate glasses have to withstand increased chemical, thermal and mechanical loads when used.
  • the substrate glasses should therefore have transformation temperatures of over 450 ° C and good resistance to temperature changes.
  • high mechanical loads occur, e.g. B. when installing clamping voltages on the axis of rotation of up to 100 N / mm 2 and in operation at high speeds of currently 3 500 to 20 000 U / min additional voltages by the centrifugal forces. Glasses with a thickness of 0.25 to 3.0 mm can withstand such loads, particularly if they are surface-tempered.
  • glasses for the use mentioned must be chemically toughened. It makes sense to prestress them by ion exchange in the salt bath below the transformation temperature T g , ie they have sufficient ions such as Li + and / or nations suitable for exchange.
  • the chemical resistance of the substrate glass is important for the functionality of a hard disk, because the read / write head glides at a distance of currently approx. 50 nm on an air cushion above the rotating hard disk. This distance must be maintained for proper functioning.
  • the surface of the hard disk substrate is not resistant to the influence of the atmosphere and a chemical attack renders the surface rough due to efflorescence even before the coating, or if the surface loses its adhesive strength to the applied layer sequence due to the influence of the atmosphere and this detaches from it, which is what turn to Functional loss or loss of function.
  • the substrates should therefore have high chemical resistance and good layer adhesion.
  • glasses suitable as hard disk substrates are their thermal expansion behavior, which does not differ too much from that of the coating materials (for example Co-alloys with thermal expansion coefficients 20 / 3oo of approx. 12 x 10 " ⁇ / K) and above everything should not differ too much from that of the materials in the fixing system of the drive (e.g. the spring steel spindle with 203 oo approx. 12 x 10 "6 / K) to avoid tension.
  • a high thermal expansion ( ⁇ 2 o / 3oo> 7.0 x 10 "6 / K) is also beneficial for the laser cutting ability of the glass, because with high thermal expansion the cutting time can be reduced, i.e. the throughput can be increased.
  • Hard disks also need a high degree of dimensional stability so that they do not flutter in the drive even at high speeds. Such deflections from the horizontal rest position would cause the read / write head to fly or slide too low, causing the read / write head to lose its orientation to the information content of the spot on the hard disk ("runout") or to collide with the hard disk ( "head crash”).
  • a requirement for materials for hard disks is therefore a high specific modulus of elasticity E / p, which means a high modulus of elasticity E and / or a low density p.
  • E / p should be more than 25 x 10 5 x Ncm / g. Similar requirements for the specific modulus of elasticity are also imposed on substrates for display applications due to the problem of "sagging" in the manufacturing process, which means the sagging of larger glass panes due to their own weight.
  • the flatness and low surface roughness properties are also suitable for display applications and for use in telecommunications technology, for. B. as a DWDM filter, an advantage.
  • the glasses in particular for the production of the mass products mentioned, should be able to be produced at low production costs.
  • the melting and hot forming behavior of the glasses must be suitable for large-scale plants.
  • the glass melts should attack the refractory material of the melting aggregates as little as possible, ie they should be producible at low temperatures and no aggressive corrosion-promoting effects. components included.
  • Suitable glasses should be industrially of sufficient internal quality (e.g. no bubbles, knots, inclusions), e.g. B. on a float system or in drawing processes, for. B. preferably in the down-draw process, economically producible.
  • the production of thin ( ⁇ 1.5 mm) streak-free substrates with low surface ripple (waviness) via drawing processes requires a high degree of devitrification stability of the glasses.
  • the glasses belong to a wide variety of glass groups, e.g. B. borosilicate glasses, zinc silicate glasses, aluminosilicate glasses and calcium silicate glasses.
  • Such glasses as described, for example, in DE 42 06 268 A1, have a very high tendency to crystallize and can therefore not be produced in the required surface qualities in the drawing process.
  • the glasses of JP 2000-007372 A which also contain Li and also P, also lead to corrosion of the refractory material during their manufacture.
  • Glasses containing ZrO 2 and glasses which contain the heavy alkaline earth oxides SrO and / or BaO also have disadvantages with regard to their producibility.
  • Li 2 O, BaO, SrO, ZrO 2 and also PbO are also present as optional components in the aluminoborosilicate glasses of JP 4-70262 B2.
  • the glasses contain zinc oxide, and the ZnO content can vary over a wide range.
  • the high ZnO-containing glasses have the disadvantage of low crystallization stability.
  • the mandatory presence of all three glass formers SiO 2 , B 2 O 3 and AI 2 O 3 makes the glasses inflexible to special production conditions.
  • the glasses contain little or no TiO 2 and little or no MgO, which is why they do not have sufficiently high moduli of elasticity.
  • the glasses contain 58 to 67% by weight, preferably 60 to 65% by weight, of the network former SiO 2 . Higher contents would make the glasses too viscous and "long", the good melting properties would be lost. At lower concentrations, the chemical resistance and mechanical stability would be impaired. In addition, the tendency to crystallize would increase significantly if the content of network formers was too low.
  • the glasses contain 1 to 5% by weight of the network former B 2 O 3 , preferably 2 to 4% by weight.
  • the minimum content ensures a sufficient proportion of glass former and good meltability. At concentrations higher than 5% by weight, the chemical resistance would deteriorate, the viscosity would increase and thus also the tendency to crystallize.
  • the glasses can also contain a third glass former, Al 2 O 3 , which stabilizes the system, namely up to 5% by weight. The good melting properties were lost at higher proportions. A content of up to 2% by weight is preferred.
  • Na 2 O is present as a flux to lower the melting temperatures and to enable chemical tempering through ion exchange in the glasses, namely with 8 to 17% by weight.
  • K 2 O can also be present in the glasses with up to 12% by weight, preferably up to 10% by weight. K 2 O promotes the interchangeability of the sodium ions.
  • the glasses do not need Li 2 O, so they are free of Li 2 O, because Li 2 O would have a very negative effect on the crystallization stability.
  • the glasses contain 3 to 12% by weight, preferably 4 to 10% by weight, of MgO. MgO is the main modulus of elasticity in these glasses. As a further modulus of elasticity, the glasses can contain up to 12% by weight of CaO, preferably up to 10% by weight. At higher levels of both MgO and CaO, the crystallization stability would deteriorate.
  • the sum of MgO and CaO is preferably at most 20% by weight.
  • the glasses contain 1 to 5% by weight, preferably 2 to 3% by weight, of TiO 2 . Higher levels would lower crystallization stability, lower levels would worsen chemical resistance.
  • the glasses can contain one or more coloring or radiation-absorbing components from the Fe 2 O 3 , CoO, CuO group , V 2 O 5 , Cr 2 O 3 contain, the content of each individual component and the content of their sum should not be more than 2 wt .-%. Higher contents would be unfavorable for the crystallization stability of the glasses.
  • ZnO is also an important component for the hot forming properties and also for the elastic modulus of the glasses. It increases the surface tension of the melt and improves the crystallization stability within the existing proportions. It is present in the glasses with at least 2% by weight and at most 8% by weight. These high levels of the important modulus of elasticity are also possible by not using lithium oxide. At even higher levels, devitrification stability would decrease.
  • the proportion of ZnO is preferably limited to a maximum of 2% by weight, since higher proportions increase the risk of disruptive ZnO deposits on the glass surface which can form in the hot-forming area through evaporation and subsequent condensation.
  • the glasses are not only free of Li 2 O, but also free of BaO and SrO, P 2 O 5 and ZrO 2 .
  • the crystallization resistance is high and, in particular due to the freedom from P 2 O 5 , the corrosion of the refractory material is low.
  • the glasses according to the invention are readily chemically toughened by ion exchange of alkali ions below the transformation temperature. Such an ion exchange can be carried out in a known manner by introducing the glass body into melts (salt baths) of more than 90% by weight of rather low-melting potassium salts, e.g. B. nitrate, or by applying pastes of higher melting potassium salts, e.g. B.
  • Exposure times and temperatures correspond to the usual conditions depending on the respective glass composition in these known ion exchange processes, ie times between 0.5 and 24 h and temperatures between T g (transformation temperature) - 100 K and T g - 50 K, that is to say temperatures for these glasses between 350 and 550 ° C, whereby lower temperatures require longer dwell times.
  • the chemical tempering enables a strong and lasting tempering to be built up, which increases the already high breaking strength of the glasses.
  • the glasses can contain conventional refining agents in conventional amounts in order to improve the glass quality. They can contain up to 1.5% by weight of As 2 O 3 , Sb 2 O 3 , SnO 2 and / or CeO 2 . It is also possible to add 1.5% by weight of CI “ , F “ or SO 2 " . The sum of As 2 O 3 , Sb 2 O 3 , CeO 2 , SnO 2 , CI “ , F “ and SO However, 4 2 " should not exceed 1.5% by weight. If the refining agents As 2 O 3 and Sb 2 O 3 are dispensed with, the glasses can be processed not only with the various drawing processes, but also with the float process.
  • Table 1 shows two examples of glasses according to the invention.
  • the table contains their composition (in% by weight on an oxide basis) and information on the essential properties of the glasses.
  • the raw materials for the oxides preferably carbonates, fluorides and / or nitrates, are weighed out, the refining agent is added and the mixture is mixed well.
  • the glass batch is melted at approx. 1500 ° C in a continuous melting unit, then refined and homogenized.
  • the glass is processed at a casting temperature of around 1350 ° C.
  • Their high chemical resistance is documented by the indication of the acid resistance class SR according to DIN 8424 and the alkali resistance class AR according to DIN 10659.
  • the glasses have an acid resistance class of 1 and an alkali resistance class of 1.
  • T g between> 450 ° C and ⁇ 610 ° C is high enough for the temperatures that occur in sputtering and other coating processes and low enough for chemical tempering through ion exchange.
  • the glasses also have a high resistance to temperature changes.
  • the coating materials to be used for the substrates the glasses have good layer adhesion.
  • the table also contains the processing temperature V A [° C], i.e. the temperature at the viscosity 10 4 dPas, which is ⁇ 1100 ° C for the glasses.
  • the glasses thus have a viscosity behavior suitable for hot forming and meltability with conventional techniques.
  • the glasses can be manufactured in conventional refractory melting units and trays.
  • the table also contains the elastic modulus E [GPa], determined on non-prestressed samples, the density p [g / cm 3 ] and the specific elastic modulus E / p [10 5 N cm / g].
  • the high modulus of elasticity E of more than 70 GPa with a low density p ⁇ 2,800 g / cm 3 and thus the high specific modulus of elasticity E / p of more than 25 x 10 5 N cm / g show the high dimensional stability of the glasses.
  • the table also contains the Knoop hardness HK 0.1 / 20 of the glasses, which is between 470 and 650.
  • the table also contains the thermal expansion coefficient ⁇ 20 / 3oo of the glasses. It is between 7 x 10 "6 / K and 10 x 10 " 6 / K and is therefore sufficiently close to the expansion coefficient of the clamping material, the drive shaft and the coating materials for hard drives.
  • Glass bodies measuring 30 mm x 30 mm x 2 mm were produced to demonstrate the chemical prestressability and were left in a bath of molten KNO 3 at 480 ° C. for 8 hours. Exchange zones with usual stress values with thicknesses of at least 10 ⁇ m could be detected using EDX.
  • the glasses can therefore be chemically tempered, which creates sufficiently thick compressive stress zones. This increases their mechanical strength, which is good in itself.
  • the glasses have a good internal quality due to their good melting, refining and workability.
  • the glasses are very stable to crystallization and can be economically produced on an industrial scale.
  • the glasses Due to their good devitrification stability and their high surface tension, the glasses can be produced not only as thicker, but also as thin ( ⁇ 1.5 mm) streak-free substrates in very good quality, especially with low (waviness ⁇ 50 nm) surface ripple, especially in a drawing process.
  • the high surface quality makes polishing easier and saves costly processing steps.
  • the glasses can be polished to a surface roughness (Ra) of ⁇ 0.5 nm.
  • compositions (% by weight on oxide basis) and essential properties of the glasses
  • the glasses according to the invention thus meet the entire requirement profile for properties in order to be suitable for the production of toughened or non-toughened hard disk substrates, even for high speeds.
  • the glasses are particularly suitable for use as substrates in telecommunications technologies, especially for DWDM filters. They are also outstandingly suitable for use as substrates in display technologies, in particular as substrates for field emission displays, so-called FEDs.
  • the glasses can be produced not only with the various drawing processes, preferably with the down-draw process, but, if they are free of As 2 O 3 and Sb 2 O 3 , also with the float process.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Life Sciences & Earth Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Geochemistry & Mineralogy (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Ceramic Engineering (AREA)
  • Inorganic Chemistry (AREA)
  • Glass Compositions (AREA)
  • Magnetic Record Carriers (AREA)

Abstract

L'invention concerne un verre borosilicate contenant de l'oxyde de zinc, dont la composition (en % en poids sur base oxyde) est la suivante : SiO2 58-67, B2O3 1-5, Al2O3 0-5, Na2O 8-17, K2O 0-12, MgO 3-12, CaO 0-12, ZnO 2-8, TiO2 1-5. Ce verre est particulièrement adapté comme substrat de disque dur.
PCT/EP2001/015065 2000-12-22 2001-12-19 Verre borosilicate contenant de l'oxyde de zinc WO2002051764A2 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
US10/451,227 US20040075086A1 (en) 2000-12-22 2001-12-19 Borosilicate glass containing zinc oxide
AU2002237247A AU2002237247A1 (en) 2000-12-22 2001-12-19 Borosilicate glass containing zinc oxide

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE10064808.8 2000-12-22
DE10064808A DE10064808B4 (de) 2000-12-22 2000-12-22 Zinkoxidhaltiges Borosilicatglas und dessen Verwendungen

Publications (2)

Publication Number Publication Date
WO2002051764A2 true WO2002051764A2 (fr) 2002-07-04
WO2002051764A3 WO2002051764A3 (fr) 2002-11-07

Family

ID=7668829

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/EP2001/015065 WO2002051764A2 (fr) 2000-12-22 2001-12-19 Verre borosilicate contenant de l'oxyde de zinc

Country Status (4)

Country Link
US (1) US20040075086A1 (fr)
AU (1) AU2002237247A1 (fr)
DE (1) DE10064808B4 (fr)
WO (1) WO2002051764A2 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2011022639A3 (fr) * 2009-08-21 2011-07-28 Corning Incorporated Verres compatibles au zircon pour étirage vers le bas

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5583606B2 (ja) 2008-02-26 2014-09-03 コーニング インコーポレイテッド ケイ酸塩ガラス用の清澄剤
US8232218B2 (en) * 2008-02-29 2012-07-31 Corning Incorporated Ion exchanged, fast cooled glasses
CN104271525A (zh) * 2012-04-27 2015-01-07 旭硝子株式会社 玻璃板
WO2013184307A2 (fr) * 2012-06-06 2013-12-12 3M Innovative Properties Company Particules de verre basse densité à basse teneur en bore

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2011022639A3 (fr) * 2009-08-21 2011-07-28 Corning Incorporated Verres compatibles au zircon pour étirage vers le bas
US8802581B2 (en) 2009-08-21 2014-08-12 Corning Incorporated Zircon compatible glasses for down draw
US9556058B2 (en) 2009-08-21 2017-01-31 Corning Incorporated Zircon compatible glasses for down draw

Also Published As

Publication number Publication date
DE10064808A1 (de) 2002-07-11
DE10064808B4 (de) 2005-09-01
US20040075086A1 (en) 2004-04-22
WO2002051764A3 (fr) 2002-11-07
AU2002237247A1 (en) 2002-07-08

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